JPS6318657B2 - - Google Patents
Info
- Publication number
- JPS6318657B2 JPS6318657B2 JP55164978A JP16497880A JPS6318657B2 JP S6318657 B2 JPS6318657 B2 JP S6318657B2 JP 55164978 A JP55164978 A JP 55164978A JP 16497880 A JP16497880 A JP 16497880A JP S6318657 B2 JPS6318657 B2 JP S6318657B2
- Authority
- JP
- Japan
- Prior art keywords
- amorphous
- alloys
- alloy
- roll method
- magnetic
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired
Links
- 229910001004 magnetic alloy Inorganic materials 0.000 claims description 16
- 229910052751 metal Inorganic materials 0.000 claims description 6
- 239000002184 metal Substances 0.000 claims description 6
- 229910052804 chromium Inorganic materials 0.000 claims description 5
- 229910052802 copper Inorganic materials 0.000 claims description 5
- 229910052719 titanium Inorganic materials 0.000 claims description 5
- 229910052721 tungsten Inorganic materials 0.000 claims description 5
- 229910052742 iron Inorganic materials 0.000 claims description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims description 4
- 229910052759 nickel Inorganic materials 0.000 claims description 4
- 229910052748 manganese Inorganic materials 0.000 claims description 3
- 239000000203 mixture Substances 0.000 claims description 3
- 229910052735 hafnium Inorganic materials 0.000 claims description 2
- 229910052726 zirconium Inorganic materials 0.000 claims description 2
- 239000012535 impurity Substances 0.000 claims 1
- 238000005096 rolling process Methods 0.000 description 23
- 229910045601 alloy Inorganic materials 0.000 description 14
- 239000000956 alloy Substances 0.000 description 14
- 229910000808 amorphous metal alloy Inorganic materials 0.000 description 11
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 8
- 238000004519 manufacturing process Methods 0.000 description 8
- 229910020630 Co Ni Inorganic materials 0.000 description 6
- 229910002440 Co–Ni Inorganic materials 0.000 description 6
- 238000000034 method Methods 0.000 description 6
- 230000005415 magnetization Effects 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 229910052723 transition metal Inorganic materials 0.000 description 4
- 150000003624 transition metals Chemical class 0.000 description 4
- 229910052796 boron Inorganic materials 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 229910052758 niobium Inorganic materials 0.000 description 3
- 238000010791 quenching Methods 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 239000011162 core material Substances 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- -1 Co Substances 0.000 description 1
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- 229910000990 Ni alloy Inorganic materials 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000003466 anti-cipated effect Effects 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 230000005389 magnetism Effects 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 230000035699 permeability Effects 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000007712 rapid solidification Methods 0.000 description 1
- 238000013341 scale-up Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Classifications
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/147—Alloys characterised by their composition
- H01F1/153—Amorphous metallic alloys, e.g. glassy metals
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C45/00—Amorphous alloys
- C22C45/008—Amorphous alloys with Fe, Co or Ni as the major constituent
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Dispersion Chemistry (AREA)
- Electromagnetism (AREA)
- Power Engineering (AREA)
- Physics & Mathematics (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Soft Magnetic Materials (AREA)
- Magnetic Heads (AREA)
- Continuous Casting (AREA)
Description
本発明は、製造が容易で、かつ機械的特性が良
好なる非晶質磁性合金に関する。
近年超急冷技術の進歩により種々の非晶質磁性
合金が得られるようになつた。歴史的にはガン法
もしくはピストンアンビル法及びスプラツトクエ
ンチング法等によりFe―P―C、Co―P―B、
Ni―Bなどの非晶質合金が得られたという報告
があり、また、P、C、Bと遷移金属の組合せに
より非晶質合金が得られる事が知られている。こ
のうち、Pは蒸気圧が高く、組成ずれが生ずる問
題や公害上の問題があり一方、Cは溶解中に遷移
金属中に固溶させるのが困難であるばかりでな
く、分離析出するなど製造上の問題点が多い。そ
の為、現在Bが最も有効な元素である事が知られ
ている。非晶質磁性合金の作製法は現在では前述
のような方法にかわつて両ロール法や片ロール法
が主流となつて来ている。これは以前の方法が不
安定形の非晶質薄片しか得られないのに対し、こ
れらの方法を用いることにより一定幅、一定厚み
のリボン形状の非晶質磁性合金を容易に得ること
ができるので工業上の利点が大きい為である。両
ロール法は容湯合金を両側より圧延急冷して非晶
質化する為片ロール法のように溶湯の片側よりの
み冷却する方法に比べて非晶質化能力は高い。し
かしながら、両ロール法の欠点は圧延急冷する
為、ロール面が損傷しやすく、又幅の広い長尺も
のの非晶質合金を得る事は非常に困難である。従
つて非晶質合金の量産という面を考えた場合、片
ロール法によらざるを得ないのが実状である。実
際現在の片ロール法では幅20cmほどの幅広非晶質
リボンが得られるのに対し、両ロール法ではせい
ぜい2cmほどの非晶質リボンしか得られていな
い。これは片ロール法では単に1個のロール幅を
広くするだけで装置的なスケールアツプは十分で
あるのに対し、両ロール法では2個のロールのス
ケールアツプのみでなく圧延する為に力学的強度
が必要となりモーターの馬力、軸受の強度などの
配慮が必要で、装置的に大がかりなものとなるか
らである。又周知のように非晶質磁性合金は極め
て硬いため両ロール法の圧延ロール表面の損傷を
無くする事は極めて難しいのに対し、片ロール法
では単に浴湯をロール面に吹きつけて急冷するだ
けであるのでロールの損傷は全く無い。これらの
事より急冷能力は低いが量産性のある片ロール法
による非晶質磁性合金の作製が現在主流になりつ
つある。ところが、遷移金属とホウ素の組合せよ
り成る組成を有する非晶質磁性合金は両ロール法
では比較的容易に1cm幅ぐらいのものが得られて
いるが、片ロール法ではせいぜい幅が1〜2mmぐ
らいのものしか得られていない。これ以上の幅の
ものを得ようとすると片ロール法では冷却が十分
でなくなるため、ロールから凝固したリボンが離
れ巻き取られる際もリボンの温度が400〜800℃ほ
どもあるため、得られたリボンが酸化し変色す
る。また、このようにして得られた非晶質磁性合
金は、本来非晶質合金がもつ180゜折り曲げに耐え
る機械的特性を有せず、極めて脆いものであつ
た。この非晶質磁性合金は機械的特性が劣るのみ
ならず、リボンが部分的に結晶化しているため、
その磁気特性もまた好ましくないものであつた。
従つて、(Fe―Co―Ni)―B系の特性良好なる
非晶質磁性合金を片ロール法で幅広のリボン形状
として得る事は極めて困難な事であつた。
また、(Fe―Co―Ni)―B系を改良した(Fe
―Co―Ni)―Zr系、(Fe―Co―Ni)―Zr―B系
などが発表されており、これらの材料は従来の
(Fe―Co―Ni)―B系に比べ容易に片ロール法
によつて幅広の非晶質リボンを得ることができ
る。しかしながら、これらのZrを含む合金系は
極めて酸化されやすいため、空気中で母合金を溶
解して片ロール法により超急冷し、非晶質合金化
するのは極めて困難である。その為、現在では真
空中もしくは不活性雰囲気中での製造がなされて
いるが、量産性及びコスト面で問題があつた。
本発明はかかる問題を解決するものであり、製
造を容易にして、かつ特性良好なる非晶質磁性合
金を提供するものである。
以下に本発明の構成を詳説する。
本発明者らは種々の添加物効果を検討した結果
この(Fe―Co―Ni)―B系に対しNbの添加が
極めて効果的で、片ロール法でも極めて容易に幅
広の非晶質磁性合金リボンが得られる事を発見し
た。
実験の結果、非晶質化しやすい組成範囲は次の
領域で与えられる合金である事がわかつた。
(Fe―Co―Ni)aNbbBc
ただし、a、b、cは原子%を示し、
a+b+c=100という条件下において、
60≦a≦95
2≦b≦30
0<c≦30
特に、幅が4cm以上、厚みが40μm以上の非晶質
リボンを容易に得ようとする場合は、
6≦b≦30
となるようにすればよい。又、非晶質合金が磁性
を有する為の条件及び空気中で非晶質合金を作製
しようとする場合、酸化させない為には、
2≦b≦20
である事が望ましい。
周知のように従来のM(=Fe、Co、Ni)100-cBc
系合金ではc≧15(原子%)でないと非晶質しに
くく、又飽和磁化σsはBの増加と伴に減少する事
が知られている。一方本発明の(M―Nb)100-cBc
系合金では上述したようにNbの多量添加により
Bが15%以下でも非晶質化するものの非磁性元素
Nbの多量添加により飽和磁化σsが、同じB含有
量では第1図に示したように従来のM100-cBc系
よりも低くなる。従つてσsの高い値を必要とする
磁気ヘツド等への応用を考えた場合本発明のM―
Nb―B系においては
c10
である事が望ましい。なお第1図は一般的傾向を
示した図であり、Nb含有量、Mの磁性元素によ
つてσsの値は多少変動する。
実施例 1
母合金を1450℃で溶解した後、耐火物製のノズ
ルよりアルゴンガス圧0.3Kg/cm2を加えて、
1400rpmで回転している直径30cmの鉄製ロールの
回転表面上に噴出させ急冷凝固させる方法を用い
て得た非晶質合金Fe5Co77Nb8B10と従来の材料を
用いトラツク幅600μmの市販の磁気ヘツド形状に
加工して、これらをコアとする磁気ヘツドを作り
耐摩耗特性およびビツカース硬度を測定した。
これらの測定結果を第1表に示した。
耐摩耗特性は、CrO2テープを4.75cm/secのス
ピードで、磁気ヘツドに圧接させつつ100時間、
走行させた後の磁気ヘツドの摩耗量(μm)で測
定した。
The present invention relates to an amorphous magnetic alloy that is easy to manufacture and has good mechanical properties. In recent years, advances in ultra-quenching technology have made it possible to obtain various amorphous magnetic alloys. Historically, Fe-P-C, Co-P-B,
There have been reports that amorphous alloys such as Ni--B have been obtained, and it is also known that amorphous alloys can be obtained by combining P, C, B, and transition metals. Among these, P has a high vapor pressure, which causes compositional deviation and pollution problems, while C is not only difficult to form into a solid solution in transition metals during melting, but also separates and precipitates during production. There are many problems with the above. Therefore, B is currently known to be the most effective element. Currently, the two-roll method and the one-roll method have become mainstream in the production of amorphous magnetic alloys, replacing the methods described above. This is because previous methods can only yield unstable amorphous flakes, whereas these methods can easily yield ribbon-shaped amorphous magnetic alloys of a constant width and thickness. This is because it has great industrial advantages. In the double roll method, the molten alloy is rolled and rapidly cooled from both sides to become amorphous, so it has a higher amorphous ability than the single roll method, which cools only one side of the molten metal. However, the disadvantage of the two-roll method is that the roll surface is easily damaged due to rapid cooling during rolling, and it is very difficult to obtain a wide and long amorphous alloy. Therefore, when considering the mass production of amorphous alloys, the reality is that the single roll method has no choice but to be used. In fact, the current single-roll method yields a wide amorphous ribbon with a width of about 20 cm, whereas the double-roll method yields an amorphous ribbon with a width of only about 2 cm. This is because in the single roll method, it is sufficient to scale up the equipment simply by widening the width of one roll, whereas in the double roll method, it is not only necessary to increase the scale of the two rolls, but also to increase the mechanical scale of the rolling process. This is because strength is required, and consideration must be given to the horsepower of the motor, the strength of the bearings, etc., and the equipment becomes large-scale. Furthermore, as is well known, since amorphous magnetic alloys are extremely hard, it is extremely difficult to eliminate damage to the rolling roll surface in the double-roll method, whereas in the single-roll method, hot water is simply sprayed onto the roll surface to rapidly cool it. There is no damage to the roll at all. For these reasons, the production of amorphous magnetic alloys by the single roll method, which has low quenching ability but is mass-producible, is now becoming mainstream. However, although it is relatively easy to obtain amorphous magnetic alloys with a composition consisting of a combination of transition metals and boron with a width of about 1 cm using the double roll method, the width of amorphous magnetic alloys consisting of a combination of transition metals and boron is about 1 to 2 mm at most when using the single roll method. I've only been able to get what I want. If you try to obtain a width wider than this, the single roll method will not provide sufficient cooling, and even when the solidified ribbon is separated from the roll and wound up, the temperature of the ribbon will be around 400 to 800 degrees Celsius. The ribbon oxidizes and discolors. Furthermore, the amorphous magnetic alloy thus obtained did not originally have the mechanical properties of an amorphous alloy to withstand 180° bending, and was extremely brittle. This amorphous magnetic alloy not only has poor mechanical properties, but also has partially crystallized ribbons.
Its magnetic properties were also unfavorable.
Therefore, it has been extremely difficult to obtain a (Fe--Co--Ni)--B based amorphous magnetic alloy with good properties in the form of a wide ribbon using the single roll method. In addition, we have improved the (Fe-Co-Ni)-B system (Fe
-Co-Ni)-Zr series, (Fe-Co-Ni)-Zr-B series, etc. have been announced, and these materials are easier to roll into single rolls than the conventional (Fe-Co-Ni)-B series. Wide amorphous ribbons can be obtained by the method. However, since these Zr-containing alloy systems are extremely easily oxidized, it is extremely difficult to melt the master alloy in air and ultra-quench it using a single roll method to form an amorphous alloy. For this reason, they are currently manufactured in a vacuum or in an inert atmosphere, but this poses problems in terms of mass production and cost. The present invention solves these problems and provides an amorphous magnetic alloy that is easy to manufacture and has good properties. The configuration of the present invention will be explained in detail below. The present inventors investigated the effects of various additives and found that the addition of Nb is extremely effective for this (Fe-Co-Ni)-B system, and it is extremely easy to create a wide amorphous magnetic alloy using the single roll method. I discovered that you can get ribbons. As a result of experiments, it was found that alloys in the following range are likely to become amorphous. (Fe-Co-Ni) a Nb b B cHowever, a, b, and c indicate atomic percent, and under the condition that a+b+c=100, 60≦a≦95 2≦b≦30 0<c≦30 Especially, If you want to easily obtain an amorphous ribbon with a width of 4 cm or more and a thickness of 40 μm or more, the following relationship may be satisfied: 6≦b≦30. Furthermore, in order to prevent oxidation, it is desirable that 2≦b≦20 be satisfied under the conditions for an amorphous alloy to have magnetism and when attempting to produce an amorphous alloy in air. As is well known, conventional M (=Fe, Co, Ni) 100-c B c
It is known that in alloys based on c≧15 (atomic %), it is difficult to form an amorphous state, and the saturation magnetization σ s decreases as B increases. On the other hand, the (M-Nb) 100-c B c of the present invention
As mentioned above, in B-type alloys, B becomes amorphous even if B is less than 15% due to the addition of a large amount of Nb, but it is a non-magnetic element.
By adding a large amount of Nb, the saturation magnetization σ s becomes lower than that of the conventional M 100-c B c system at the same B content, as shown in FIG. Therefore, when considering application to magnetic heads etc. that require a high value of σs , the M-
In the Nb-B system, c10 is desirable. Note that FIG. 1 is a diagram showing a general tendency, and the value of σ s varies somewhat depending on the Nb content and the magnetic element of M. Example 1 After melting the master alloy at 1450°C, an argon gas pressure of 0.3 kg/cm 2 was applied through a refractory nozzle.
Commercially available amorphous alloy Fe 5 Co 77 Nb 8 B 10 with a track width of 600 μm was obtained using a method of rapid solidification by jetting it onto the rotating surface of a 30 cm diameter iron roll rotating at 1400 rpm and a conventional material. A magnetic head was fabricated using these as a core, and its wear resistance and Vickers hardness were measured. The results of these measurements are shown in Table 1. The abrasion resistance properties are as follows: The CrO 2 tape was pressed against the magnetic head at a speed of 4.75cm/sec for 100 hours.
The amount of wear (μm) on the magnetic head after running was measured.
【表】
第1表に示すように、本実施例のNbを添加し
た非晶質合金は優れた耐摩耗特性を有する。従つ
て、オーデイオ用のみでなくV.T.R用磁気ヘツド
コア材としても本実施例の材料は有効である。
(FeXCoYNiZ)Nb B系材料にNbの外に、Cr、
Mo、W、Cu、Tiを添加し、前記実施例1と同様
の方法により非晶質合金を作り諸特性を測定し、
その結果次の事がわかつた。
この系にCr、Mo、WをNbと共に添加するこ
とにより、透磁率の優れた非晶質合金が得られ
た。
この系にCuをNbと共に添加することにより、
磁歪の少ない非晶質合金が得られた。
この系にTiをNbと共に添加することにより、
機械的強度の優れた非晶質合金が得られた。
ただし、Ti、Cr、Mo、W、Mn、Cuのみで
Nbを添加しない場合、一定形状の靭性を有する
幅2cm以上の幅広非晶質リボンを片ロール法によ
り得る事は不可能であり、又これらの元素を10%
以上添加するとむしろ非晶質化が困難となる。よ
つてNbの添加効果と組合せて、はじめて実用的
な諸特性が得られるわけである。上述した合金は
高純度要素から作られる。しかしながら、これら
合金の利用においてはそれらが、少量の他元素を
溶解している、安価な市販材料から作られること
が予想される。しかがつて本発明で考慮されてい
る合金は他元素をわずかに含有してもよく、これ
らの他元素は市販品のFeまたはNi合金中に、例
えば原料金属の供給源の結果としてか、その後の
添加中の出来事によりよく発見される。
これらの元素の実例はMn、Zr、Hfなどであ
る。
実施例 2
実施例1と同様の方法により(Co.855Nb.145)100
−XBX系を作製し、その飽和磁化σs、結晶化温度
TX、キユリー温度TCのB含有量依存性を調べた。
第2図に結果を示した。σsは従来のM(=Fe、
Co、Ni)―B系非晶質合金と同様B含有量の増
加と伴に減少するが、Nbの多量添加によりその
値が低くなつている為、磁気ヘツド等への応用を
考えた場合B含有量は10%以下にする事が望まし
い事がわかつた。
以上のように、本発明によれば、製造容易で、
熱的安定性の優れた幅広の非晶質磁性合金を提供
することができる。また本発明のようにNbの他
にCr、Mo、W、Cu、Tiなどを添加することに
より諸特性の優れた幅広の非晶質磁性合金を提供
することができる。[Table] As shown in Table 1, the Nb-added amorphous alloy of this example has excellent wear resistance properties. Therefore, the material of this example is effective not only for audio but also as a magnetic head core material for VTR. (Fe X Co Y Ni Z )Nb In addition to Nb, Cr,
Adding Mo, W, Cu, and Ti, an amorphous alloy was made in the same manner as in Example 1, and various properties were measured.
As a result, we found out the following. By adding Cr, Mo, and W together with Nb to this system, an amorphous alloy with excellent magnetic permeability was obtained. By adding Cu and Nb to this system,
An amorphous alloy with low magnetostriction was obtained. By adding Ti and Nb to this system,
An amorphous alloy with excellent mechanical strength was obtained. However, only Ti, Cr, Mo, W, Mn, and Cu
If Nb is not added, it is impossible to obtain a wide amorphous ribbon with a width of 2 cm or more with a certain shape and toughness by the single roll method.
Adding more than this makes it rather difficult to make it amorphous. Therefore, various practical properties can only be obtained when combined with the effect of Nb addition. The alloys described above are made from high purity elements. However, in the use of these alloys it is anticipated that they will be made from inexpensive commercially available materials that have small amounts of other elements dissolved in them. However, the alloys contemplated by the present invention may also contain trace amounts of other elements, which may be present in the commercially available Fe or Ni alloys, for example as a result of the source of the raw metal or subsequently. Often discovered due to events during the addition of Examples of these elements are Mn, Zr, Hf, etc. Example 2 By the same method as Example 1 (Co .855 Nb .145 ) 100
-X B _
The dependence of T X and the Curie temperature T C on B content was investigated.
The results are shown in Figure 2. σ s is the conventional M (=Fe,
Co, Ni) - As with B-based amorphous alloys, it decreases as the B content increases, but the value becomes lower with the addition of a large amount of Nb, so when considering applications such as magnetic heads, B It was found that it is desirable to keep the content below 10%. As described above, according to the present invention, manufacturing is easy;
A wide range of amorphous magnetic alloys with excellent thermal stability can be provided. Furthermore, by adding Cr, Mo, W, Cu, Ti, etc. in addition to Nb as in the present invention, a wide range of amorphous magnetic alloys with excellent properties can be provided.
第1図は飽和磁化σsとB含有量との関係を示す
図、第2図は飽和磁化σs、キユリー温度TC、結
晶化温度TXとB含有量との関係を示す図である。
Figure 1 is a diagram showing the relationship between saturation magnetization σ s and B content, and Figure 2 is a diagram showing the relationship between saturation magnetization σ s , Curie temperature T C , crystallization temperature T X and B content. .
Claims (1)
れる金属またはそれらの混合物;a、bおよびc
は原子%であり、かつそれらの和が100になると
いう条件でそれぞれ 60≦a≦95、6≦b≦20、0<c≦10)で示され
ることを特徴とする非晶質磁性合金。 2 不純物元素としてMn、Zr、Hfを含む事を特
徴とする特許請求の範囲第1項記載の非晶質磁性
合金。 3 式:MaTbBc (式中MはFe、CoおよびNiからなる群から選ば
れる金属またはそれらの混合物;TはNbを主成
分とし、かつCuまたはTiのいずれかの金属もし
くはCr、MoおよびWのうちの少なくとも1種の
金属を10原子%以下含有する混合物;a、bおよ
びcは原子%であり、かつそれらの和が100にな
るという条件下で、それぞれ60≦a≦95、6≦b
≦20、0<c≦10)で示されることを特徴とする
非晶質磁性合金。[Claims] 1 Formula: M a Nb b B c (wherein M is a metal selected from the group consisting of Fe, Co and Ni or a mixture thereof; a, b and c
60≦a≦95, 6≦b≦20, and 0<c≦10), respectively, with the condition that is atomic % and the sum of these is 100. 2. The amorphous magnetic alloy according to claim 1, which contains Mn, Zr, and Hf as impurity elements. 3 Formula: M a T b B c (wherein M is a metal selected from the group consisting of Fe, Co and Ni, or a mixture thereof; T is a metal whose main component is Nb and either Cu or Ti or Cr , Mo and W, each containing 10 atomic % or less of at least one metal; a, b and c are atomic %, and each of 60≦a≦, provided that their sum is 100. 95, 6≦b
≦20, 0<c≦10).
Priority Applications (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP55164978A JPS5789450A (en) | 1980-11-21 | 1980-11-21 | Amorphous magnetic alloy |
US06/321,560 US4437912A (en) | 1980-11-21 | 1981-11-16 | Amorphous magnetic alloys |
DE3146031A DE3146031C2 (en) | 1980-11-21 | 1981-11-20 | Amorphous magnetic alloys |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP55164978A JPS5789450A (en) | 1980-11-21 | 1980-11-21 | Amorphous magnetic alloy |
Related Child Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP1059927A Division JPH0765147B2 (en) | 1989-03-13 | 1989-03-13 | Amorphous magnetic alloy |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS5789450A JPS5789450A (en) | 1982-06-03 |
JPS6318657B2 true JPS6318657B2 (en) | 1988-04-19 |
Family
ID=15803499
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP55164978A Granted JPS5789450A (en) | 1980-11-21 | 1980-11-21 | Amorphous magnetic alloy |
Country Status (3)
Country | Link |
---|---|
US (1) | US4437912A (en) |
JP (1) | JPS5789450A (en) |
DE (1) | DE3146031C2 (en) |
Families Citing this family (20)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS6030734B2 (en) * | 1979-04-11 | 1985-07-18 | 健 増本 | Amorphous alloy containing iron group elements and zirconium with low brittleness and excellent thermal stability |
JPS606907Y2 (en) * | 1980-12-05 | 1985-03-07 | ソニー株式会社 | sliding member |
JPS58147538A (en) * | 1982-02-25 | 1983-09-02 | Hiroyasu Fujimori | Sputtered amorphous magnetic material and its manufacture |
JPS58185747A (en) * | 1982-04-21 | 1983-10-29 | Toshiba Corp | Amorphous iron alloy for magnetic head |
JPS59193235A (en) * | 1983-04-15 | 1984-11-01 | Hitachi Ltd | Co-nb-zr type amorphous magnetic alloy and magnetic head using the same |
US4743513A (en) * | 1983-06-10 | 1988-05-10 | Dresser Industries, Inc. | Wear-resistant amorphous materials and articles, and process for preparation thereof |
EP0191107B1 (en) * | 1984-07-27 | 1992-01-29 | Research Development Corporation of Japan | Amorphous material which operates magnetically |
JPH0615706B2 (en) * | 1985-03-14 | 1994-03-02 | 三井造船株式会社 | High corrosion resistant amorphous alloy |
DE3616008C2 (en) * | 1985-08-06 | 1994-07-28 | Mitsui Shipbuilding Eng | Highly corrosion-resistant, glass-like alloy |
US4897318A (en) * | 1986-01-21 | 1990-01-30 | Matsushita Electric Industrial Co., Ltd. | Laminated magnetic materials |
NL8802873A (en) * | 1988-11-22 | 1990-06-18 | Philips Nv | SOFT MAGNETIC MULTILAYER FILM AND MAGNETIC HEAD EQUIPPED WITH SUCH A SOFT MAGNETIC MULTI LAYER FILM. |
US7591910B2 (en) * | 2002-12-04 | 2009-09-22 | California Institute Of Technology | Bulk amorphous refractory glasses based on the Ni(-Cu-)-Ti(-Zr)-Al alloy system |
US7186306B2 (en) * | 2003-02-14 | 2007-03-06 | The Nanosteel Company | Method of modifying iron based glasses to increase crystallization temperature without changing melting temperature |
US20060042938A1 (en) * | 2004-09-01 | 2006-03-02 | Heraeus, Inc. | Sputter target material for improved magnetic layer |
US20060286414A1 (en) * | 2005-06-15 | 2006-12-21 | Heraeus, Inc. | Enhanced oxide-containing sputter target alloy compositions |
US20070253103A1 (en) * | 2006-04-27 | 2007-11-01 | Heraeus, Inc. | Soft magnetic underlayer in magnetic media and soft magnetic alloy based sputter target |
WO2009127665A1 (en) * | 2008-04-15 | 2009-10-22 | Ocas Onderzoekscentrum Voor Aanwending Van Staal N.V. | Amorphous alloy and process for producing products made thereof |
US20110293463A1 (en) * | 2010-05-27 | 2011-12-01 | Daniel James Branagan | Alloys exhibiting spinodal glass matrix microconstituents structure and deformation mechanisms |
PL234845B1 (en) * | 2018-05-25 | 2020-04-30 | Politechnika Czestochowska | Amorphous volumetric alloy |
US11688551B2 (en) * | 2020-01-24 | 2023-06-27 | Toyota Jidosha Kabushiki Kaisha | Method for producing metal foils |
Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5472715A (en) * | 1977-11-24 | 1979-06-11 | Toshiba Corp | High permeability amorphous alloy |
JPS5489918A (en) * | 1977-12-28 | 1979-07-17 | Toshiba Corp | High permeability amorphous alloy |
JPS54107824A (en) * | 1978-02-13 | 1979-08-24 | Toshiba Corp | High permeability amorphous alloy |
JPS54107825A (en) * | 1978-02-13 | 1979-08-24 | Toshiba Corp | High permeability amorphous alloy |
Family Cites Families (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB1505841A (en) | 1974-01-12 | 1978-03-30 | Watanabe H | Iron-chromium amorphous alloys |
US4067732A (en) | 1975-06-26 | 1978-01-10 | Allied Chemical Corporation | Amorphous alloys which include iron group elements and boron |
US4056411A (en) | 1976-05-14 | 1977-11-01 | Ho Sou Chen | Method of making magnetic devices including amorphous alloys |
US4116682A (en) | 1976-12-27 | 1978-09-26 | Polk Donald E | Amorphous metal alloys and products thereof |
US4152144A (en) | 1976-12-29 | 1979-05-01 | Allied Chemical Corporation | Metallic glasses having a combination of high permeability, low magnetostriction, low ac core loss and high thermal stability |
US4137075A (en) | 1977-01-17 | 1979-01-30 | Allied Chemical Corporation | Metallic glasses with a combination of high crystallization temperatures and high hardness values |
US4188211A (en) | 1977-02-18 | 1980-02-12 | Tdk Electronics Company, Limited | Thermally stable amorphous magnetic alloy |
US4221592A (en) | 1977-09-02 | 1980-09-09 | Allied Chemical Corporation | Glassy alloys which include iron group elements and boron |
US4225339A (en) * | 1977-12-28 | 1980-09-30 | Tokyo Shibaura Denki Kabushiki Kaisha | Amorphous alloy of high magnetic permeability |
WO1979000674A1 (en) | 1978-02-03 | 1979-09-20 | Shin Gijutsu Kaihatsu Jigyodan | Amorphous carbon alloys and articles manufactured therefrom |
-
1980
- 1980-11-21 JP JP55164978A patent/JPS5789450A/en active Granted
-
1981
- 1981-11-16 US US06/321,560 patent/US4437912A/en not_active Expired - Lifetime
- 1981-11-20 DE DE3146031A patent/DE3146031C2/en not_active Expired
Patent Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5472715A (en) * | 1977-11-24 | 1979-06-11 | Toshiba Corp | High permeability amorphous alloy |
JPS5489918A (en) * | 1977-12-28 | 1979-07-17 | Toshiba Corp | High permeability amorphous alloy |
JPS54107824A (en) * | 1978-02-13 | 1979-08-24 | Toshiba Corp | High permeability amorphous alloy |
JPS54107825A (en) * | 1978-02-13 | 1979-08-24 | Toshiba Corp | High permeability amorphous alloy |
Also Published As
Publication number | Publication date |
---|---|
JPS5789450A (en) | 1982-06-03 |
US4437912A (en) | 1984-03-20 |
DE3146031A1 (en) | 1982-07-15 |
DE3146031C2 (en) | 1986-11-27 |
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